|Publication number||US7629267 B2|
|Application number||US 11/370,228|
|Publication date||Dec 8, 2009|
|Filing date||Mar 6, 2006|
|Priority date||Mar 7, 2005|
|Also published as||US20060199357|
|Publication number||11370228, 370228, US 7629267 B2, US 7629267B2, US-B2-7629267, US7629267 B2, US7629267B2|
|Inventors||Yuet Mei Wan, René de Blank, Jan Willem Maes|
|Original Assignee||Asm International N.V.|
|Export Citation||BiBTeX, EndNote, RefMan|
|Patent Citations (108), Non-Patent Citations (9), Referenced by (35), Classifications (12), Legal Events (5)|
|External Links: USPTO, USPTO Assignment, Espacenet|
This application claims the priority benefit under 35 U.S.C. § 119(e) of U.S. Provisional Application 60/659,454, filed Mar. 7, 2005.
In addition, this application is related to: U.S. Patent Application No. 60/605,068, STOICHIOMETRIC SILICON COMPOUNDS DEPOSITION IN BATCH FURNACES, filed Aug. 27, 2004; U.S. patent application Ser. No. 10/623,482, METHOD TO FORM ULTRA HIGH QUALITY SILICON-CONTAINING LAYERS, filed Jul. 18, 2003, which claims the priority benefit of U.S. Provisional Application No. 60/397,576, METHOD TO FORM ULTRA HIGH QUALITY SILICON-CONTAINING LAYERS, filed Jul. 19, 2002; U.S. patent application Ser. No. 10/074,564, THIN FILMS AND METHODS OF MAKING THEM, filed Feb. 11, 2002; and U.S. patent application Ser. No. 10/074,563, IMPROVED PROCESS FOR DEPOSITION OF SEMICONDUCTOR FILMS, filed Feb. 11, 2002. The disclosure of each of these references is incorporated herein by reference in its entirety.
1. Field of the Invention
This invention relates generally to forming silicon-containing layers during integrated circuit fabrication and, more particularly, to methods for forming silicon-containing layers with increased tensile stress.
2. Description of the Related Art
As the dimensions of microelectronic devices become smaller, the physical characteristics of the deposited layers, including uniformity in thickness, composition, and coverage, become more important. This is particularly true of the layers, or films, of silicon compounds that can act as dielectrics or insulators to separate conductive elements of an integrated circuit. For example, silicon nitride materials are widely used in the semiconductor industry as transistor gate dielectrics, insulators between metal levels, barriers to prevent oxidation and other diffusion, hard masks, passivation layers, spacer materials in transistors, anti-reflective coating materials, layers in non-volatile memories, etc. Silicon oxide and silicon carbide materials are similarly common in integrated circuit fabrication.
Currently, chemical vapor deposition (CVD) is the most commonly used process for deposition of thin layers on a substrate. With this process, precursors for molecules or atoms that will ultimately form the deposited layer are fed simultaneously into a reaction chamber as molecular precursors. The substrate is kept at a temperature that is optimized to promote chemical reaction between the molecular precursors so that a layer of the desired atomic or molecular species is deposited on the substrate. The most common molecular precursor for forming silicon-containing thin layers by conventional CVD has been silane.
CVD has proven to have a superior ability to deposit layers with relatively uniform thicknesses. In addition, it produces relatively conformal layers, i.e., layers that closely replicate the shape of the surface on which they are being deposited. However, as device density continues to increase and geometries continue to become more complicated, deposition processes have been further refined to meet the need for even more uniform and conformal layers.
For these reasons, atomic layer deposition (ALD) has become more prominent in semiconductor fabrication. ALD typically involves multiple deposition cycles, with each cycle depositing a thin layer. ALD seeks to deposit perfectly conformal and uniform layers by depositing no more than a single monolayer during each cycle. Typically, this is accomplished by use of a self-terminating precursor molecule and optimizing conditions to avoid condensation and thermal decomposition of the precursors. For example, to deposit a layer of a titanium compound, a titanium precursor molecule such as TiCl4 can be used. With TiCl4, the titanium atom attaches to the surface of the substrate while chlorine atoms terminate the adsorbed layer on the side of the titanium atom opposite the substrate surface. As a result, once the substrate surface is covered with a monolayer of the titanium molecule, the top of the titanium layer will comprise chlorine atoms which are relatively inert and cause the adsorption process to self-terminate.
In contrast to CVD, ALD molecular precursors used to produce a compound layer, i.e., a layer comprising two or more elements, are typically introduced into the ALD reactor in separate pulses. For example, a first precursor self-limitingly adsorbs on the substrate in a first pulse, with ligands of the adsorbed species preventing further adsorption. Between introduction of precursors, the reaction chamber is evacuated or purged with inert gas to prevent gas phase reactions between the different precursors. After purging of the first precursor, a second precursor can be introduced into the reaction chamber to react with the layer deposited by introduction of the first precursor, e.g., to strip the ligands or to replace the ligands. In this way, one cycle is completed and one thin compound layer is deposited on a substrate. After reaction with the second precursor, the second precursor (and any byproduct) can be removed by evacuation or inert gas purging. In addition to these precursors, other reactants can also be pulsed into the reaction chamber during each cycle. The cycle can then be repeated until a compound layer of a desired thickness is reached.
While ALD gives superior conformality and uniformity in comparison to CVD, ALD is relatively inefficient in terms of speed. Because a layer of a desired thickness must, in theory, be formed one molecular monolayer at a time (in actuality, less than one molecular monolayer is typical, due to the blocking of reactive sites as a result of steric hindrance), and because multiple steps must be employed to form each monolayer, ALD forms a layer with a given thickness more slowly than does CVD. Consequently, while conformality and uniformity is increased, ALD has the drawback of having decreased throughput in comparison to CVD.
Nevertheless, high conformality and uniformity are important considerations as semiconductor fabrication currently involves depositing silicon-containing compound films during the process of making thousands or even millions of devices simultaneously on a substrate that is 200 millimeters (mm) in diameter. Moreover, the industry is transitioning to 300 mm wafers, and can use even larger wafers in the future. In addition, even larger substrates, in the form of flat panel displays, etc., are becoming increasingly common. Significant variations in the thickness and/or composition of the silicon-containing compound films during the manufacturing process can lead to lower manufacturing yields when the affected devices do not meet the required performance specifications. Also, variations across the film within a particular device can reduce device performance and/or reliability. Thus, as substrate sizes increase to accommodate manufacture of larger numbers of microelectronic devices on a circuit, the problems created by the shortcomings of conventional CVD processes also increase.
In addition, when silicon-containing compound films, such as silicon nitride films, are used to form liners for electrical devices such as transistors, high stress is desirable to enhance carrier mobility in the transistor channel. A common technique for forming such silicon nitride films is low pressure CVD (LPCVD). Films formed by such a process, however, result in films with relatively low tensile stress.
Consequently, there is a need for methods for forming high quality silicon-containing compound films, such as silicon nitride films, with high stress.
According to one aspect of the invention, a method is provided for forming a silicon-containing compound layer. The method comprises loading a substrate into a reactor and depositing a silicon layer on the substrate by exposing the substrate to a flow of trisilane. The flow of trisilane is interrupted and a silicon compound layer is formed by exposing the silicon layer to a reactive nitrogen species while the flow is interrupted. The substrate is also exposed to a flow of a dopant precursor.
According to another aspect of the invention, an integrated circuit is provided. The integrated circuit comprises a film silicon nitride comprising a dopant. The tensile stress of the film is about 2 GPa or greater.
According to yet another aspect of the invention, a method is provided for semiconductor processing. The method comprises repeatedly separately exposing a substrate to a silane and a first reactive species to form a silicon-containing film. The tensile stress of the silicon-containing film is increased by exposing the substrate to a second reactive species.
The invention will be better understood from the detailed description of the preferred embodiments and from the appended drawings, which are meant to illustrate and not to limit the invention, wherein like numerals refer to like structures throughout and wherein:
Stoichiometric silicon nitride liner layers can be formed by LPCVD using dichlorosilane or trisilane. These layers typically have a maximum tensile stress of about 1.1 GPa. A high stress layer of about 2 GPa or higher, however, is preferred for modern silicon nitride liner layers.
Plasma-enhanced CVD (PECVD) can be used to form a high stress silicon nitride layer. Besides the power of the plasma source and the pressure of the PECVD process, the temperatures of post-processing, implantation and etch conditions can be manipulated to control the intrinsic stress of the nitride layer. It is easier, however, to obtain high compressive stress with PECVD than high tensile stress.
Advantageously, it has been found that the tensile stress of a silicon nitride layer can be increased by adding a dopant, e.g., carbon, to the layer. In preferred embodiments of the invention, a silicon-containing layer, e.g., a silicon nitride layer, is formed by exposing a substrate to a silane and to a first reactive species, e.g., a nitrogen-containing precursor, in separate pulses. The silane is preferably trisilane. Other examples of silanes include monosilane, disilane, dichlorosilane and trichlorosilane. The substrate is also exposed to a dopant precursor, e.g., a carbon-containing precursor. The substrate can be exposed to the dopant precursor concurrently with exposure of the substrate to the silane and/or concurrently with exposure of the substrate to the first reactive species or in pulse(s) separate from exposure of the substrate to the silane or the first reactive species. Advantageously, addition of the dopant increases the tensile stress of the silicon-containing films, thereby forming films having a tensile stress of about 2 GPa or higher.
Reference will now be made to the FIGURES, in which like numerals refer to like parts throughout.
Single Wafer Reactor
Use of a single-substrate, horizontal flow cold-wall reactor has particular advantages. For example, the illustrated single-pass horizontal flow design enables laminar flow of reactant gases, with low residence times, which in turn facilitates rapid sequential processing, particularly in the cyclical deposition process described below, while minimizing reactant interaction with each other and with chamber surfaces. Such a laminar flow enables sequentially flowing reactants that might react with each other. Reactions to be avoided include highly exothermic or explosive reactions, such as produced by oxygen and hydrogen-bearing reactants, and reactions that produce particulate contamination of the chamber. The skilled artisan will recognize, however, that for certain sequential processes, other reactor designs can also be provided for achieving these ends, provided sufficient purge or evacuation times are allowed to remove incompatible reactants.
A plurality of radiant heat sources are supported outside the chamber 12 to provide heat energy in the chamber 12 without appreciable absorption by the quartz chamber 12 walls. The illustrated radiant heat sources comprise an upper heating assembly of elongated tube-type radiant heating elements 13. The upper heating elements 13 are preferably disposed in spaced-apart parallel relationship and also substantially parallel with the reactant gas flow path through the underlying reaction chamber 12. A lower heating assembly comprises similar elongated tube-type radiant heating elements 14 below the reaction chamber 12, preferably oriented transverse to the upper heating elements 13. Desirably, a portion of the radiant heat is diffusely reflected into the chamber 12 by rough specular reflector plates above and below the upper and lower lamps 13, 14, respectively. Additionally, a plurality of spot lamps 15 supply concentrated heat to the underside of the substrate support structure (described below), to counteract a heat sink effect created by cold support structures extending through the bottom of the reaction chamber 12.
Each of the elongated tube type heating elements 13, 14 is preferably a high intensity tungsten filament lamp having a transparent quartz envelope containing a halogen gas, such as iodine. Such lamps produce full-spectrum radiant heat energy transmitted through the walls of the reaction chamber 12 without appreciable absorption. As is known in the art of semiconductor processing equipment, the power of the various lamps 13, 14, 15 can be controlled independently or in grouped zones in response to temperature sensors. The skilled artisan will appreciate, however, that the principles and advantages of the processes described herein can be achieved with other heating and temperature control systems.
A substrate, preferably comprising a silicon wafer 16, is shown supported within the reaction chamber 12 upon a substrate support structure 18. Note that, while the substrate of the illustrated embodiment is a single-crystal silicon wafer, it will be understood that the term “substrate” broadly refers to any surface on which a layer is to be deposited. Moreover, thin, uniform layers are often required on other substrates, including, without limitation, the deposition of optical thin films on glass or other substrates.
The illustrated support structure 18 includes a substrate holder 20, upon which the wafer 16 rests, and which is in turn supported by a support spider 22. The spider 22 is mounted to a shaft 24, which extends downwardly through a tube 26 depending from the chamber lower wall. Preferably, the tube 26 communicates with a source of purge or sweep gas which can flow during processing, inhibiting process gases from escaping to the lower section of the chamber 12.
A plurality of temperature sensors are positioned in proximity to the wafer 16. The temperature sensors can take any of a variety of forms, such as optical pyrometers or thermocouples. The number and positions of the temperature sensors are selected to promote temperature uniformity, as will be understood in light of the description below of the preferred temperature controller. In the illustrated reaction 10, the temperature sensors directly or indirectly sense the temperature of positions in proximity to the wafer.
In the illustrated embodiment, the temperature sensors comprise thermocouples, including a first or central thermocouple 28, suspended below the wafer holder 20 in any suitable fashion. The illustrated central thermocouple 28 passes through the spider 22 in proximity to the wafer holder 20. The reactor 10 further includes a plurality of secondary or peripheral thermocouples, also in proximity to the wafer 16, including a leading edge or front thermocouple 29, a trailing edge or rear thermocouple 30, and a side thermocouple (not shown). Each of the peripheral thermocouples are housed within a slip ring 32, which surrounds the substrate holder 20 and the wafer 16. Each of the central and peripheral thermocouples are connected to a temperature controller, which sets the power of the various heating elements 13, 14, 15 in response to the readings of the thermocouples.
In addition to housing the peripheral thermocouples, the slip ring 32 absorbs and emits radiant heat during high temperature processing, such that it compensates for a tendency toward greater heat loss or absorption at wafer edges, a phenomenon which is known to occur due to a greater ratio of surface area to volume in regions near such edges. By minimizing edge losses, the slip ring 32 can reduce the risk of radial temperature non-uniformities across the wafer 16. The slip ring 32 can be suspended by any suitable means. For example, the illustrated slip ring 32 rests upon elbows 34 which depend from a front chamber divider 36 and a rear chamber divider 38. The dividers 36, 38 desirably are formed of quartz. In some arrangements, the rear divider 38 can be omitted.
The illustrated reaction chamber 12 includes an inlet port 40 for the injection of reactant and carrier gases, and the wafer 16 can also be received therethrough. An outlet port 42 is on the opposite side of the chamber 12, with the wafer support structure 18 positioned between the inlet 40 and outlet 42.
An inlet component 50 is fitted to the reaction chamber 12, adapted to surround the inlet port 40, and includes a horizontally elongated slot 52 through which the wafer 16 can be inserted. A generally vertical inlet 54 receives gases from remote sources, as will be described more fully with respect to
An outlet component 56 similarly mounts to the process chamber 12 such that an exhaust opening 58 aligns with the outlet port 42 and leads to exhaust conduits 59. The conduits 59, in turn, can communicate with suitable vacuum means (not shown) for drawing process gases through the chamber 12. In the preferred embodiment, process gases are drawn through the reaction chamber 12 and a downstream scrubber 88 (
The reactor 10 also includes a source 60 of excited species, preferably positioned upstream from the chamber 10. The excited species source 60 of the illustrated embodiment comprises a remote plasma generator, including a magnetron power generator and an applicator along a gas line 62. An exemplary remote plasma generator is available commercially under the trade name TRW-850 from Rapid Reactive Radicals Technology (R3T) GmbH of Munich, Germany. In the illustrated embodiment, microwave energy from a magnetron is coupled to a flowing gas in an applicator along a gas line 62. A source of precursor gases 63 is coupled to the gas line 62 for introduction into the excited species generator 60. The illustrated embodiment employs nitrogen gas, flowed through an excited species generator to generate nitrogen radicals, as a precursor gas. A separate source of carrier gas 64 can also be coupled to the gas line 62, though in embodiments employing N2 as the nitrogen source, separate carrier gas can be omitted. One or more further branch lines 65 can also be provided for additional reactants. Each gas line can be provided with a separate mass flow controller (MFC) and valves, as shown, to allow selection of relative amounts of carrier and reactant species introduced to the generator 60 and thence into the reaction chamber 12.
Wafers are preferably passed from a handling chamber (not shown), which is isolated from the surrounding environment, through the slot 52 by a pick-up device. The handling chamber and the process chamber 12 are preferably separated by a gate valve (not shown), such as a slit valve with a vertical actuator, or a valve of the type disclosed in U.S. Pat. No. 4,828,224.
The total volume capacity of a single-wafer process chamber 12 designed for processing 200 mm wafers, for example, is preferably less than about 30 liters, more preferably less than about 20 liters, and most preferably less than about 10. The illustrated chamber 12 has a capacity of about 7.5 liters. Because the illustrated chamber 12 is divided by the dividers 36, 38, wafer holder 20, ring 32, and the purge gas flowing from the tube 26, however, the effective volume through which process gases flow is around half the total volume (about 3.77 liters in the illustrated embodiment). Of course, it will be understood that the volume of the single-wafer process chamber 12 can be different, depending upon the size of the wafers for which the chamber 12 is designed to accommodate. For example, a single-wafer process chamber 12 of the illustrated type, but for 300 mm wafers, preferably has a capacity of less than about 100 liters, more preferably less than about 60 liters, and most preferably less than about 30 liters. One 300 mm wafer process chamber has a total volume of about 24 liters, with an effective processing gas capacity of about 11.83 liters. The relatively small volumes of such chambers desirably allow rapid evacuation or purging of the chamber between phases of the cyclical process described below.
At least one dopant source 77 is also provided. The dopant source 77 preferably comprises a carbon-containing precursor. Exemplary carbon-containing precursors include mono-methyl silane, di-methyl silane, tri-methyl silane, tetra-methyl silane, mono-methyl disilane, di-methyl disilane, tri-methyl disilane, tetra-methyl disilane, mono-methyl trisilane, di-methyl trisilane, tri-methyl trisilane, tetra-methyl trisilane, methane, ethane, propane, butane, acetylene and combinations thereof. In other embodiments, the dopant source 77 can include a germanium precursor.
As also shown in
The preferred reactor 10 also includes a source 73 of nitrogen gas (N2). As is known in the art, N2 is often employed in place of H2 as a carrier or purge gas in semiconductor fabrication. Nitrogen gas is relatively inert and compatible with many integrated materials and process flows. Other possible carrier gases include noble gases, such as helium (He) or argon (Ar).
In addition, another source 63 of nitrogen, such as diatomic nitrogen (N2), can be provided to a remote plasma generator 60 to provide active species for reaction with deposited silicon layers in the chamber 12. An ammonia (NH3) source 84 can additionally or alternatively be provided to serve as a volatile nitrogen source for thermal nitridation. Moreover, as is known in the art, any other suitable nitrogen precursor can be employed and flowed directly, or through remote plasma generator 60, into the chamber 12. In other arrangements, the gas source 63 can comprise a source of other reactant radicals for forming silicon-containing compound layers (e.g., O, C, Ge, metal, etc.).
The reactor 10 can also be provided with a source 70 of oxidizing agent or oxidant. The oxidant source 70 can comprise any of a number of known oxidants, particularly a volatile oxidant such as O2, NO, H2O, N2O, HCOOH, HClO3.
Desirably, the reactor 10 can also include other precursor gases in additional dopant sources (e.g., the illustrated phosphine 76, arsine 78 and diborane 80 sources) and etchants for cleaning the reactor walls and other internal components (e.g., HCl source 82 or NF3/Cl2 (not shown) provided through the excited species generator 60). A source of silane 86 can also be provided, e.g., for deposition of a silicon layer after a first silicon layer has been deposited using a polysilane, as discussed below.
Each of the gas sources can be connected to the inlet 54 (
As discussed above, in addition to conventional gas sources, the preferred reactor 10 includes the excited species source 60 positioned remotely or upstream of the reaction chamber 12. The illustrated source 60 couples microwave energy to gas flowing in an applicator, where the gas includes reactant precursors from the reactant source 63. A plasma is ignited within the applicator, and excited species are carried toward the chamber 12. Preferably, of the excited species generated by the source 60, overly reactive ionic species substantially recombine prior to entry into the chamber 12. On the other hand, nitrogen radicals can survive to enter the chamber 12 and react as appropriate. Advantageously, the excited species generated by the source 60 enters the chamber 12 downstream of the main process gas inlet 40, relative to flowing the reactive species through the inlet 40, thereby shortening the path of reactive species to the substrate 16 and allowing more of the nitrogen radicals to survive.
Additionally, the plasma can be generated in situ, in the reaction chamber. Such an in situ plasma, however, may cause damage, uniformity and roughness problems with some deposited layers. Consequently, where a plasma is used, a remotely generated plasma is typically preferred.
While some preferred embodiments are presented in the context of a single-substrate, horizontal flow cold-wall reactor, it will be understood that certain aspects of the invention will have application to various types of reactors known in the art and that the invention is not limited to such a reactor. For example, batch reactors can be used and advantageously allow for increased throughput due to the ability to simultaneously process a plurality of wafers. Further details regarding deposition in a batch reactor are disclosed below.
With reference to
In a preferred embodiment, inside the process chamber 526, gas is flowed in a generally upward direction 552 and then removed from the reaction space 529 via the exhaust space 554 between the process chamber 526 and the liner 528, where gas flows in a downward direction 556 to the exhaust 558, which is connected to a pump (not shown). The gas injector 540 preferably distributes process gases inside the process chamber 526 over the entire height of the reaction space 529. The gas injector 540 itself acts as a restriction on the flow of gas, such that the holes 548 that are closer to the conduit 544 tend to inject more gas into the reaction space than those holes 548 that are farther from the conduit 544. Preferably, this tendency for differences in gas flows through the holes 548 can be compensated to an extent by reducing the distance between the holes 548 (i.e., increasing the density of the holes 548) as they are located farther away from the conduit 544. In other embodiments, the size of individual holes making up the holes 548 can increase with increasing distance from the conduit 544, or both the size of the holes 548 can increase and also the distance between the holes 548 can decrease with increasing distance from the conduit 544. Advantageously, however, the preferred embodiments are illustrated with holes 548 of constant size so as to minimize the surface area of the sides of the gas injector 540 containing the holes 548.
The injector 540 is advantageously designed to reduce the pressure inside the gas injector, resulting in a reduction of the gas phase reactions within the injector, since reaction rates typically increase with increasing pressure. While such reduced pressure can also lead to a poor distribution of gas over the height of the gas injector 540, the distribution of holes 548 across the height of the injector 540 is selected to improve uniformity of gas distribution.
The gas injector 540 in accordance with one illustrative embodiment of the present invention is shown in
The gas injector 540 is provided with a pattern of holes 548 substantially extending over the height 560 (
With reference to
The cross-section of
In a preferred embodiment, two precursor gases can each be injected via their own separate gas injectors 540 (not shown), so that they are first mixed after being injected into the reaction space 529 (
Advantageously, the use of two gas injector parts 541 and 542 allows for further tuning possibilities. The flows supplied to the different gas injector parts 541, 542 can be chosen differently to fine-tune the gas flow into the reaction space 529. This will improve uniformity in the deposition rates of precursors over the height 560 of the wafer load 550 (
With reference to
The use of a remote MRG unit is particularly applicable to the pulsed trisilane process of the preferred embodiments. Unlike most batch processes, the nitridation (or other compound forming step) of the preferred embodiments is a self-limiting process, such that uniformity of radical distribution within the process chamber 526 is not essential. Over-reaction is not a concern from a result point of view. Nevertheless, non-uniformity of radical distribution is disadvantageous because it will prolong the nitridation process; nitridation would need to be conducted for a longer time to ensure complete nitridation across each wafer at every vertical position within the process chamber 526. Furthermore, aside from uniformity issues, the distance traversed from the plasma cavity 582 to the process chamber 526, and within the process chamber 526 to reach each wafer, leads to a relatively low radical survival rate due to the number of collisions en route that cause recombination.
With reference to
With reference to
In operation, a current is applied to the coil. A readily available radio frequency (RF) power source, e.g., 13.56 MHz, can be employed for this purpose. Process gases surrounding the plasma source 590, outside the insulating sleeve 594 but inside the process chamber 526, are ignited in an annulus surrounding the plasma source 590. Due to the proximity to the wafers 550, lower power can be employed, compared to use of a remote plasma generator. Symmetry of distribution across the wafers can be provided by rotating the wafer boat during operation.
A silane is preferably used as the silicon precursor. The silane can be selected from the group consisting of monosilane (SiH4), a polysilane and a chlorosilane (SiH4−nCln, where n=1 to 4).
Preferably, a polysilane is used as the silane to form the silicon layer 100. As used herein, a “polysilane” has the chemical formula SinH2n+2, where n=2 to 4. Preferably, the polysilane is disilane or trisilane. Most preferably, the polysilane is trisilane. Consequently, while the invention is described in the context of particularly preferred embodiments employing CVD cycles with trisilane, the skilled artisan will appreciate, in view of the present disclosure, that certain advantages of the described processes can be obtained with other precursors and/or other deposition techniques.
Trisilane (H3SiSiH2SiH3 or Si3H8) offers substantial benefits when used as a silicon precursor, as disclosed in U.S. application Ser. No. 10/623,482, filed Jul. 18, 2003; U.S. application Ser. No. 10/074,564, filed Feb. 11, 2002; and published PCT Application WO 02/064,853, published Aug. 2, 2002, the disclosures of which are hereby incorporated by reference in their entireties. For example, films can be deposited with trisilane at substantially lower temperatures than with other silicon precursors, such as silane. Moreover, deposition rates with trisilane are relatively insensitive to substrate material and thickness. Also, trisilane has an extremely short film nucleation time, which reduces the size of localized crystalline deposits of silicon. As a result, deposited silicon films can be made thinner, while still being uniform. Moreover, the films will show reduced surface roughness due to the reduced size of the localized silicon deposits.
In addition, with regards to process throughput, trisilane exhibits higher deposition rates relative to silane. Trisilane also reduces thermal budgets, since it allows use of lower process temperatures than does silane.
Thus, employing trisilane in the deposition methods described herein provides numerous advantages. For example, these deposition methods enable the production of silicon-containing compound films that are uniformly thin and continuous. These advantages, in turn, enable devices to be produced in higher yields, and also enable the production of new devices having smaller circuit dimensions and/or higher reliability. These and other advantages are discussed below.
As described in greater detail below, in forming a silicon-containing compound layer, a thin silicon layer is desirably deposited on a substrate by first exposing the substrate to a silicon precursor, preferably, trisilane. The silicon layer can then be reacted with another reactive species to form a silicon-containing compound layer. In a preferred embodiment, the other reactive species is a reactive nitrogen species. The reactive nitrogen species is introduced into the reaction chamber to nitride the silicon layer and form silicon nitride. Nitridation occurs when silicon in the silicon layer reacts with nitrogen from the reactive nitrogen species to produce silicon nitride. The nitridation is preferably limited to the silicon layer on the surface of the substrate and advantageously results in a substantially perfect stoichiometry in the reaction of the silicon layer with the reactive nitrogen species. Such a complete reaction allows less incorporated impurities, denser films, and improved thickness control and step coverage. In addition, stoichiometric silicon nitride layers have improved insulating properties, and can be made thicker than conventional insulating thin films, increasing the effectiveness of these deposited layers as diffusion barriers.
In other embodiments, the silicon layer can be reacted with reactants other than nitrogen to form other silicon-containing compound layers. For example, the silicon layer can be oxidized to form a silicon oxide layer. In such a case, an oxygen precursor can be used in place of a nitrogen precursor. The oxygen precursor can include, for example, atomic oxygen, water, ozone, oxygen, nitric oxide, nitrous oxide or other oxidants known in the art. Likewise, other precursors, known in the art, can be used to form silicon-containing compound layers including, but not limited to, silicon germanium, silicon carbide, metal silicides, etc.
In addition, multiple sequential cycles of these depositions and reactions can be performed to build up a silicon-containing compound layer to a desired thickness. Advantageously, different silicon-containing compound layers formed by the methods of the present invention can be formed one over another. For example, a silicon nitride film can be deposited over a silicon oxide film. In addition, the silicon-containing compound layer can be doped or otherwise further reacted. For example, a silicon nitride layer can be oxidized to form a silicon oxynitride layer.
During each of these cycles, a dopant is preferably added to the films to increase the tensile stress of the silicon-containing compound layers. The dopant is preferably carbon (where the film is not a silicon carbide film) or germanium (where the film is not a silicon germanium film). The substrate can be exposed to the dopant at any point(s) during a reaction cycle.
In step 100, a silicon layer is formed on a substrate. “Substrate” is used herein in its usual sense to include any underlying surface onto which a silicon-containing material is deposited or applied in accordance with the preferred embodiments of the present invention. Preferred substrates can be made of virtually any material, including without limitation metal, silicon, germanium, plastic, and/or glass, preferably silicon compounds (including Si—O—C—H low dielectric constant films) and silicon alloys. Substrates can also have on them physical structures such as trenches or steps.
In forming 100 the silicon layer, deposition from a silicon precursor can be suitably conducted according to various deposition methods known to those skilled in the art, but the greatest benefits are obtained when deposition is conducted according to the CVD methods taught herein. The disclosed methods can be suitably practiced by employing CVD, including plasma-enhanced chemical vapor deposition (PECVD) or thermal CVD, utilizing gaseous trisilane to deposit a silicon-containing compound film onto a substrate contained within a CVD chamber. Thermal CVD is preferred for the silicon deposition phases of the process.
The polysilane is preferably introduced into the process chamber 12 (
Where the polysilane is trisilane, the trisilane is preferably introduced into the chamber by way of a bubbler used with a carrier gas to entrain trisilane vapor, more preferably a temperature controlled bubbler.
Preferably, process conditions are tailored to processing in the particular type of reactor in which substrates are loaded. In general, deposition conditions are created to supply sufficient energy to pyrollize or decompose the silicon precursor on a hot substrate surface. For depositions in a single substrate reactor, the process conditions preferably allow a silicon deposition rate that is controlled primarily by the rate at which the silicon precursor is delivered to the substrate surface. Thus, for precursors such as trisilane, deposition is preferably conducted under chemical vapor deposition conditions that are in or near the mass transport limited regime. In the mass transport limited regime, deposition rates are essentially independent of temperature. Under such a regime small temperature variations across the surface of the substrate have little or no effect on deposition rate. It has been found that deposition in the mass transport limited regime greatly minimizes thickness and compositional variations and enables the production of the preferred silicon-containing compound films described herein. Thus, advantageously, such conditions allow for deposition with minimal loading effects or pattern sensitivity.
For such a single substrate reactor, the trisilane flow rate from the bubbler preferably is about 1 sccm to 1 slm, more preferably about 50 sccm to about 500 sccm. Preferably, the carrier gas has a flow rate is about 2 slm to about 20 slm.
The total pressure in the reaction chamber 12 (
Advantageously, deposition in the pressure range of 0.001 Torr to 10 Torr results in excellent uniformity. In addition, low partial pressures are generally desirable to maintain a lower hydrogen content during the process. Due to the inherently lower H:Si ratio in silanes with higher numbers of silicon atoms, however, the partial pressure for, e.g., trisilane can be higher than that for lower order silanes, such as disilane and silane.
Preferably, silicon layer formation 100, and the cycle 140 generally, is performed isothermally. For thermal CVD, preferred deposition temperatures are in the range of about 400° C. to about 800° C., preferably about 450° C. to about 750° C., more preferably about 450° C. to about 650° C. Preferably, these temperatures correspond to the temperature setting for the substrate.
For depositions in a batch reactor, deposition conditions are preferably established so that the reaction rate of the silicon precursor is the limiting variable for the silicon deposition rate. Unlike single-wafer systems, batch systems, such as that of the illustrated vertical reactor, encounter difficulties in achieving an even distribution of precursor vapors across all wafers within the reaction tube in the mass transport limited regime. On the other hand, batch systems can often employ principles of hot wall reactors to achieve highly uniform temperature distributions. As a result, rather than the mass transport limited regime, the pulsed deposition is preferably conducted under reaction kinetics limited conditions, also known as the kinetic regime, wherein deposition rates are sensitive to temperature changes but relatively insensitive to supplied reactant concentrations.
It will be appreciated that a shift from mass transport limited to reaction kinetics limited is primarily achieved by a reduction in temperature. This results in a reduced film deposition rate that is preferable in a batch furnace. Because of the large batch size, an adequate throughput can still be achieved at a deposition rate that results from temperatures shifted down into the reaction rate limited regime. Advantageously, trisilane enables acceptable deposition rates at very low temperatures, allowing a considerably reduced consumption of thermal budgets. As the skilled artisan will readily appreciate, thermal budgets are constantly reduced as critical dimensions are scaled down, tolerances for diffusion are reduced, and new materials with lower resistance to thermal processing are introduced. The process is preferably operated at a temperature below about 600° C. and more preferably at a temperature below about 500° C., and even more preferably at a temperature between about 300° C. and about 500° C.
In addition to temperature, the skilled artisan will appreciate that the kinetic regime is partially dependent upon the reactant supply or partial pressure of trisilane. As long as the reaction rate is slower than the rate at which reactant is supplied, uniformity in a properly tuned batch furnace (in which uniform temperatures can be maintained) is excellent. Reference is made to Sze, VLSI TECHNOLOGY, pp. 240-41 (1988), the disclosure of which is incorporated herein by reference. In the illustrated batch reactors, process pressure is maintained at about 10 Torr or below and more preferably about 1 Torr or below. Trisilane preferably is supplied at less than about 100 sccm trisilane, and more preferably, at about 20 sccm. These flow rates preferably correspond to less than about 400.1 mg/minute and, more preferably, to about 80 mg/minute of trisilane flow into the reaction chamber of the reactor. The trisilane is typically diluted with a flow of a non-reactive or inert gas such as N2, H2, Ar or He. The trisilane partial pressure is thus preferably below about 10 mTorr, more preferably about 3-4 mTorr.
With continued reference to
After silicon layer formation 100, any excess silicon precursor and byproduct can be removed 110 from the process chamber. Silicon precursor removal 110 can occur by any one, or any combination of removal processes, including the following: purging of the process chamber with inert gas, evacuation of the silicon precursor, or displacement of the silicon precursor gas by a gas carrying a reactive species. Where silicon precursor gas removal 110 is accomplished by displacement of the precursor gas with a gas carrying a reactive species, however, the process chamber is preferably a single substrate laminar flow chamber such as an ASM Epsilon™ series single wafer reactor, described above and illustrated in
It will be appreciated that silicon precursor gas removal 110 is preferably performed such that the quantity of a particular reactant in the chamber 12 (
With continued reference to
As discussed above, the nitrogen radicals can be generated in various ways. In preferred embodiments, the nitrogen radicals are generated by the application of a high frequency electrical power, preferably in the GHz range. For example, using microwave energy, the remote plasma generator 60 (
In another example, for the batch reaction chamber 526 (
It will be appreciated that formation of the silicon-compound layer 120 can include reaction of the silicon layer with more than one reactive species, even where the atomic species of interest for the different reactive species is the same. For example, where the atomic species of interest is nitrogen to form silicon nitride layers, a beneficial effect is observed by the use of an NH3 flow in addition to a nitrogen radical flow. This NH3 is fed directly in the process tube, rather than via the radical generator. Although non-activated NH3 reacts minimally with silicon at temperatures below 500° C., it has been found that the addition of non-activated NH3 to the nitrogen radicals results in a more fully nitrided amorphous silicon layer, as evidenced by a lowered refractive index. Without being limited by theory, it is believed that the nitrogen radicals from a remote plasma generator activate the ammonia within the process chamber. In contrast, nitrogen radicals alone leave a slightly silicon-rich silicon nitride film, as evidenced by a slightly higher refractive index. It has also been found that ammonia provided through the remote MRG actually decreased the nitridation effect, even relative to nitrogen radicals alone.
With reference to
Accordingly, performance of the steps 100, 110, 120, and 130 comprises one cycle 140 and deposits one layer of a silicon-containing compound on a substrate. The cycle 140 can then be repeated in sequence until the silicon-containing compound layers are built up to a desired thickness.
At any time during the cycle, a dopant precursor can be introduced into the reaction chamber 12 (
Preferably, the dopant is carbon. Exemplary carbon precursors include mono-methyl silane, di-methyl silane, tri-methyl silane, tetra-methyl silane, mono-methyl disilane, di-methyl disilane, tri-methyl disilane, tetra-methyl disilane, mono-methyl trisilane, di-methyl trisilane, tri-methyl trisilane, tetra-methyl trisilane, methane, ethane, propane, butane, acetylene and combinations thereof. Preferably, the carbon precursor is a methyl silane, having one or more silicon-carbon bonds and having no carbon-carbon bonds. Such a compound has relatively weak silicon-hydrogen and carbon-hydrogen bonds. These bonds can be broken at relatively low temperatures, thus allowing the use of low processing temperatures. Mono-methyl silane is particularly advantageous because of its high vapor pressure. In addition to carbon, an example of another dopant is germanium.
In some embodiments, to increase the dopant level, it will be appreciated that the dopant can be introduced into the reaction chamber one or more times during a cycle 140. Alternatively, the duration that a dopant is introduced into the chamber can be increased to achieve the same effect. In addition, the dopant concentration can be controlled by the appropriate selection of a dopant precursor. For example, where a higher carbon concentration is desired, the dopant precursor can be selected based upon the number of silicon-carbon bonds present in the precursor. For example, rather than mono-methyl silane, tetra-methyl silane can be used.
The skilled artisan will appreciate that the present invention allows for the formation of layers of various thicknesses, a thickness being selected, for example, based upon the requirements of a particular application. For instance, for use as a transistor liner, sufficient cycles are preferably conducted to grow a silicon nitride layer between about 100 Å and 2000 Å in thickness. It will be appreciated, however, that greater thicknesses are possible; for example, thicknesses up to about 5000 Å can be formed after performing a sufficient number of cycles.
As noted above, the present invention can be utilized to form a carbon doped silicon nitride layers.
While the preferred embodiments allow silicon layers or carbon doped silicon layers of various thicknesses to be formed, preferably, the silicon layer thickness is chosen based upon nitridation conditions. This is because, during nitridation of a silicon layer atomic nitrogen can diffuse through the silicon layer and into the underlying silicon substrate. The depth of this nitrogen diffusion can be measured, as known in the art, and is related to various process conditions, including nitridation temperature and duration of nitridation. Thus, for a given set of process conditions, atomic nitrogen will diffuse into, and possibly through, the silicon layer to a particular depth, called the nitridation saturation depth. When nitridation occurs for less than about one minute, the nitridation saturation depth can be termed the short-term nitridation saturation depth.
As discussed below in the discussion of the Deposited Silicon-containing Compound Layers, nitridation of the substrate has been found to result in silicon nitride layers with dielectric properties which are inferior to what is theoretically expected. Thus, to improve the dielectric properties of deposited silicon nitride films, nitridation of the underlying substrate is preferably minimized, preferably by depositing the first silicon layer formed over a substrate to a thickness equal to or greater than the nitridation saturation depth. It will be appreciated that subsequently deposited layers will typically be spaced farther from the substrate than the nitridation saturation depth as a consequence of being deposited over this first silicon layer. As a consequence, the thickness of silicon layers deposited after the first layer preferably are less than or equal to the nitridation saturation depth.
For a given set of nitridation conditions, however, after forming the first silicon layer, silicon layers formed in subsequent cycles can be thinner since the nitridation saturation depth remains relatively constant while the silicon nitride layer thickness increases. For example, in preferred embodiments, the first silicon layer can be deposited to about the nitridation saturation depth, e.g., about 8 to 20 Å, and subsequent layers can be deposited to a thinner thickness, e.g., about 3 Å to 10 Å per cycle. In one preferred embodiment, the first silicon layer is deposited to a thickness of about 12 Å and subsequent layers are deposited to a thinner thickness of about 6 Å per cycle. In addition to varying the thickness of the silicon layer, it will be appreciated that other process conditions, such as the nitridation temperature and/or the duration of nitridation, can be varied so that the nitridation saturation depth is not deeper than the thickness of the silicon layer.
In the embodiment shown in
Atomic nitrogen is preferably generated using an excited species generator. Nitrogen gas preferably is flowed through the excited species generator at about 1 slm to about 10 slm to generate the atomic nitrogen. More preferably, the nitrogen flow is combined with a carrier gas of helium, the carrier gas preferably having a flow between about 1 slm to 10 slm.
Any excess reactive nitrogen species is then preferably removed 306 from the reaction chamber by, e.g., purging the chamber with inert gas. The steps 300-306 constitute a cycle 380 which can be repeated until a layer of a desired thickness is formed.
Accordingly, preferred embodiments for a process to form carbon doped silicon nitride layers include the following steps for introduction of reactants:
Separated pulses of silicon precursor and nitrogen reactive species
Pulse of carbon precursor.
In one preferred embodiment, reactants are introduced as follows:
Pulse of silicon precursor and carbon precursor
Pulse of reactive nitrogen species
In an alternative embodiment, a process to form carbon doped silicon nitride includes the following steps for introduction of precursors:
Pulse of silicon precursor
Pulse of reactive nitrogen species and carbon precursor
In yet another embodiment a process to form carbon doped silicon nitride includes the following steps for introduction of precursors:
Pulse of silicon precursor
Pulse of reactive nitrogen species
Pulse of carbon precursor
Pulse of reactive nitrogen species.
With reference to
It will be appreciated that different silicon precursors can be used in different cycles 140 (
It will be further appreciated that the temperatures for different steps can be different. In one preferred embodiment in a single substrate reactor, a silicon layer formation 100 (
In addition, where the reaction chamber is a vertical batch reaction chamber, the precursor gases can be introduced in various ways. For example, all gases can be provided through the bottom of the vertical reactor and exhausted from the top, or vice versa. Optionally, the gases can be injected via gas injection tubes or multiple hole injectors (see
It will also be appreciated that modifications to the batch reactor, or to the way of operating the batch reactor, known in the art, can be applied to improve the performance of this process. For example it is possible to use a holder boat or ring boat to improve the uniformity of film deposition over each wafer.
Deposited Silicon-Containing Compound Layers
Desirably, preferred silicon-containing compound films according to the preferred embodiments have a high tensile stress. Advantageously, a tensile stress of 2 GPa or greater can be achieved by doping a silicon nitride film with a carbon dopant. A tensile stress of that level allows the silicon nitride film to be used in transistor liner applications, as illustrated in
In addition, the films have a thickness that is highly uniform across the surface of the film. Film thickness uniformity is preferably determined by making multiple-point thickness measurements, e.g., by ellipsometry or cross-sectioning, determining the mean thickness by averaging the various thickness measurements, and determining the rms variability. To enable comparisons over a given surface area, the results can be expressed as percent non-uniformity, calculated by dividing the rms thickness variability by the average thickness and multiplying by 100 to express the result as a percentage. Preferably, the thickness non-uniformity is about 20% or less, more preferably about 10% or less, even more preferably about 5% or less, most preferably about 2% or less.
In addition to thickness uniformity, preferred silicon-containing compound films preferably provide a conformal coating over varied topography. A conformal coating is a layer that follows the curvature, if any, of the structure that it overlies. The conformal silicon-containing compound films preferably exhibit good step coverage. “Step coverage” refers to the thickness uniformity of a conformal film that overlies a stepped surface. A stepped surface is a surface that has two or more parallel components that are not disposed in the same horizontal plane. Step coverage is preferably determined by measuring the average thickness of the film at the bottom of the step, dividing it by the average thickness at the top of the step, and multiplying by 100 to express the result in percentage terms.
The preferred silicon-containing compound films have good step coverage even at relatively high aspect ratios. “Aspect ratio” refers to the ratio of the vertical height of the step to the horizontal width of the structure. At an aspect ratio in the range of about 4.5 to about 6, preferred silicon-containing compound films have a step coverage of about 70% or greater, more preferably 80% or greater. At an aspect ratio in the range of about 1 to about 4, preferred silicon-containing compound films have a step coverage of about 80% or greater, more preferably 90% or greater. Step coverage is preferably calculated as stated above, but can also be calculated by taking into account sidewall thicknesses. For example, alternate definitions of step coverage involve the ratio of the sidewall thickness to the average thickness at the top and/or bottom of the step. However, unless otherwise stated, step coverage herein is determined as stated above by measuring the average thickness of the horizontal portions of the silicon-containing compound film at the bottom of the step, dividing it by the average thickness of the horizontal portions at the top of the step, and multiplying by 100 to express the result in percentages.
Advantageously, surface smoothness and thickness of the preferred silicon-containing compound films are maintained over a surface area of about one square micron (μm2) or greater, more preferably about 5 μm2 or greater, even more preferably about 10 μm or greater. The silicon-containing compound film can cover all or part of a large substrate, e.g., a wafer, and thus can have a surface area of about 300 cm2 or greater, preferably about 700 cm2 or greater.
A carbon doped silicon nitride layer is formed in a batch A412™ reactor from ASM International N.V. of Bilthoven, The Netherlands. For this purpose, a batch of 50 wafers having a diameter of 200 mm is loaded into a wafer boat. The wafer boat is preferably provided with rings which surrounded the edges of the wafers to improve uniformity of the deposited film at those edges. The temperature of the wafers is allowed to stabilize such that the temperature across each wafer is uniform at between about 300° C. and about 500° C., more preferably, each wafer is at a temperature of about 435° C. The boat is preferably rotated about a vertical axis within the reaction chamber. The pressure is preferably set to between about 100 m Torr and about 10 Torr. Trisilane diluted with inert gas is flowed into the reaction chamber at a flow of 20 sccm concurrently with a flow of mono-methyl silane of about 20 sccm, the trisilane partial pressure preferably being 4 mTorr and the exposure time being 5 minutes. During this time a carbon doped silicon film of about 5 Å thick will be deposited. The trisilane flow and mono-methyl silane flow is then interrupted. Nitridation is then performed by providing 5 slm N2 to the reaction chamber for 4 minutes. During that time, the N2 is intermittently activated in four cycles of 30 seconds on 30 seconds off using a power of 3000 Watts.
It will be appreciated by those skilled in the art that various omissions, additions and modifications can be made to the processes described above without departing from the scope of the invention, and all such modifications and changes are intended to fall within the scope of the invention, as defined by the appended claims.
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|U.S. Classification||438/758, 257/E21.247|
|International Classification||H01L21/469, H01L21/31|
|Cooperative Classification||H01L29/7843, H01L21/3185, H01L21/67115, H01L21/3115, H01L29/7833, C23C16/345, H01L21/67017, C23C16/45523|
|May 10, 2006||AS||Assignment|
Owner name: ASM INTERNATIONAL N.V., NETHERLANDS
Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:WAN, YUET MEI;DE BLANK, RENE;MAES, JAN WILLEM;REEL/FRAME:017893/0928;SIGNING DATES FROM 20060415 TO 20060418
|May 18, 2010||CC||Certificate of correction|
|Nov 2, 2010||CC||Certificate of correction|
|Mar 8, 2013||FPAY||Fee payment|
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|May 25, 2017||FPAY||Fee payment|
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